Carbon-sulfur composite, preparation method therefor, and lithium secondary battery comprising same

ABSTRACT

A carbon-sulfur composite including a carbonized metal-organic framework (MOF); and a sulfur compound introduced to at least a part of an outside surface and an inside of the carbonized metal-organic framework, wherein the carbonized metal-organic framework has a specific surface area of 2500 m 2 /g to 4000 m 2 /g, and the carbonized metal-organic framework has a pore volume of 0.1 cc/g to 10 cc/g, and a method for preparing the same.

This application is a Continuation of application Ser. No. 17/964,649filed on Oct. 12, 2022, which is a Continuation of application Ser. No.16/646,080 filed on Mar. 10, 2020 (now U.S. Pat. No. 11,502,289 issuedon Nov. 15, 2022), which is the U.S. National Phase ofPCT/KR2018/011064, filed Sep. 19, 2018, and which claims priority under35 U.S.C. § 119(a) to Application No. 10-2017-0125909 filed in Korea, onSep. 28, 2017, the entire contents of all of which are expresslyincorporated by reference into the present application.

TECHNICAL FIELD

The present invention relates to a carbon-sulfur composite, a method forpreparing the same and a lithium secondary battery including the same.

BACKGROUND ART

Interests in energy storage technologies have been increasingly growingrecently. As applications have expanded to energy of mobile phones,camcorders and notebook PCs, and furthermore, to electric vehicles,efforts on the research and development of electrochemical devices havebeen more and more materialized.

Electrochemical devices are fields receiving most attention in suchaspects and among these, development of secondary batteries capable ofcharge and discharge have been the focus of attention, and developingsuch batteries has been progressed to research and development on thedesign of new electrodes and batteries for enhancing capacity densityand specific energy.

Among currently used secondary batteries, lithium secondary batteriesdeveloped in early 1990s have received attention with advantages ofhaving high operating voltage and significantly higher energy densitycompared to conventional batteries such as Ni-MH, Ni—Cd and sulfuricacid-lead batteries using an aqueous electrolyte solution.

Particularly, lithium-sulfur (Li—S) batteries are a secondary batteryusing a sulfur series material having sulfur-sulfur bonds as a positiveelectrode active material, and using lithium metal as a negativeelectrode active material. Sulfur, a main material of a positiveelectrode active material, has advantages of being very abundant inresources, having no toxicity and having a low atomic weight. Inaddition, a lithium-sulfur battery has theoretical discharge capacity of1675 mAh/g-sulfur and theoretical energy density of 2,600 Wh/kg, whichis very high compared to theoretical energy density of other batterysystems (Ni-MH battery: 450 Wh/kg, Li—FeS battery: 480 Wh/kg, Li—MnO₂battery: 1,000 Wh/kg, Na—S battery: 800 Wh/kg) currently studied, andtherefore, is a most promising battery among batteries that have beendeveloped so far.

During a discharge reaction of a lithium-sulfur battery, an oxidationreaction of lithium occurs in a negative electrode (anode), and areduction reaction of sulfur occurs in a positive electrode (cathode).Sulfur has a cyclic S₈ structure before discharge, and electric energyis stored and produced using an oxidation-reduction reaction in which anoxidation number of S decreases as S—S bonds are broken during areduction reaction (discharge), and an oxidation number of S increasesas S—S bonds are formed again during an oxidation reaction (charge).During such a reaction, the sulfur is converted to linear-structuredlithium polysulfide (Li₂S_(x), x=8, 6, 4 and 2) from cyclic S₈ by thereduction reaction, and as a result, lithium sulfide (Li₂S) is lastlyproduced when such lithium polysulfide is completely reduced. By theprocess of being reduced to each lithium polysulfide, a dischargebehavior of a lithium-sulfur battery shows gradual discharging voltagesunlike lithium ion batteries.

However, in such a lithium-sulfur battery, problems of low electricconductivity of sulfur, lithium polysulfide elution and volume expansionproblem during charge and discharge and low coulombic efficiency causedtherefrom, and a rapid capacity decrease caused from charge anddischarge need to be resolved.

Porous carbon materials are widely used in a lithium sulfur battery witha role of providing conductivity by compositing with sulfur, an activematerial of a lithium sulfur battery. Studies on enhancing batteryperformance by controlling sizes and volumes of pores formed inside suchporous carbon materials have been continuously conducted. Among these, ametal-organic framework (MOF) has an advantage in that porous carbonmaterials having a high specific surface area of 1000 m²/g to 4000 m²/gmay be synthesized by forming pores with various sizes depending on thetypes of organic molecules or metal atoms forming the MOF. However, asdescribed in Adv. Funct. Mater. 2016, 26, 8746-8756, technologies ofusing existing MOF materials in a lithium sulfur battery throughcarbonization have had a problem in that metal carbide needs to be usedas well since performance is not favorable when actually used inbatteries.

PRIOR ART DOCUMENTS

-   (Non-patent Document 1) “3D Metal Carbide®Mesoporous Carbon Hybrid    Architecture as a New Polysulfide Reservoir for Lithium-Sulfur    Batteries”, Weizhai Bao, Dawei Su, Wenxue Zhang, Xin Guo, and Guoxiu    Wang*, Adv. Funct. Mater. 2016, 26, 8746-8756

DISCLOSURE Technical Problem

As a result of extensive studies in view of the above, the inventors ofthe present invention have identified carbonizationtemperature-dependent cell performance by adjusting a temperature of acarbonization process and thereby identified the importance of acarbonization temperature. It was identified that further developing apore structure by increasing a carbonization temperature becomes animportant parameter in cell performance. In view of the above, theinventors of the present invention have identified that, whencompositing MOF-5 derived mesoporous carbon with sulfur, an activematerial, and using the result in a lithium sulfur battery,electrochemical performance of the lithium-sulfur battery such asinitial discharge capacity or cycle retaining capacity may be improved,and have completed the present invention.

Accordingly, an aspect of the present invention provides a carbon-sulfurcomposite capable of enhancing cell performance just by adjusting acarbonization temperature without introducing other methods, and amethod for preparing the same.

Technical Solution

According to an aspect of the present invention, there is provided acarbon-sulfur composite including a carbonized metal-organic framework(MOF); and a sulfur compound introduced to at least a part of an outsidesurface and an inside of the carbonized metal-organic framework, whereinthe carbonized metal-organic framework has a specific surface area of2,000 m²/g to 3,500 m²/g, and the carbonized metal-organic framework hasa pore volume of 2.2 cc/g or greater.

According to another aspect of the present invention, there is provideda method for preparing a carbon-sulfur composite including (a) preparinga carbonized metal-organic framework (MOF) by carbonizing ametal-organic framework (MOF) to 950° C. or higher; and (b) preparing acarbon-sulfur composite by mixing the metal-organic framework (MOF)carbonized in (a) with a sulfur compound.

According to another aspect of the present invention, there is provideda positive electrode including the carbon-sulfur composite.

According to still another aspect of the present invention, there isprovided a lithium secondary battery including the positive electrode; anegative electrode; and an electrolyte.

Advantageous Effects

The present invention is effective in improving electrochemicalperformance of a lithium-sulfur battery such as initial dischargecapacity or cycle retaining capacity just by adjusting a carbonizationtemperature without introducing other methods.

DESCRIPTION OF DRAWINGS

FIG. 1 is a graph showing an N₂ adsorption/desorption isotherm ofsulfur-carbon composites according to an example and a comparativeexample of the present invention.

FIG. 2 is a graph showing results of quenched solid density functionaltheory analyses on sulfur-carbon composites according to an example anda comparative example of the present invention.

FIG. 3 is a graph showing an N₂ adsorption/desorption isotherm of asulfur-carbon composite according to another comparative example of thepresent invention.

FIG. 4 shows SEM images of sulfur-carbon composites according to anexample and a comparative example of the present invention.

FIG. 5 is a graph showing initial charge and discharge properties oflithium-sulfur batteries manufactured with sulfur-carbon composites ofan example and a comparative example of the present invention.

FIG. 6 is a graph showing initial charge and discharge properties of alithium-sulfur battery manufactured with a sulfur-carbon composite ofanother comparative example of the present invention.

FIG. 7 is a graph showing initial charge and discharge properties of alithium-sulfur battery manufactured with a sulfur-carbon composite ofstill another comparative example of the present invention.

FIG. 8 is a graph showing charge and discharge efficiency oflithium-sulfur batteries of sulfur-carbon composites according to anexample and a comparative example of the present invention.

BEST MODE

Hereinafter, the present invention will be described in detail withreference to accompanying drawings so that those skilled in the art mayreadily implement the present invention. However, the present inventionmay be embodied in various different forms, and is not limited to thepresent specification.

In the drawings, parts not relevant to the descriptions are not includedin order to clearly describe the present invention, and like referencenumerals are used for like elements throughout the specification. Inaddition, sizes and relative sizes of constituents shown in the drawingsare unrelated to actual scales, and may be reduced or exaggerated forclarity of the descriptions.

A carbon-sulfur composite of the present invention includes a carbonizedmetal-organic framework (MOF); and a sulfur compound introduced to atleast a part of an outside surface and an inside of the carbonizedmetal-organic framework.

Carbonized Metal-Organic Framework

The carbon-sulfur composite of the present invention includes acarbonized metal-organic framework (MOF).

A metal-organic framework (MOF) is a porous material forming aone-dimensional, two-dimensional or three-dimensional skeleton bycoordinate bonds of inorganic nodes (metal ion or metal oxide cluster)and multitopic organic linkers being crosslinked, and is referred to asa “porous coordination polymer” or a “porous organic-inorganic hybridmaterial”. The metal-organic framework has a coordinately vacant site ona metal center as well as having a well-defined pore, and has been usedin adsorbents, gas storage materials, sensors, membranes, functionalthin films, drug delivery materials, catalysts, catalyst supports andthe like to capture guest molecules or separate molecules, and recentlyhas been actively studied.

Such a metal-organic framework may be normally prepared using a methodof a solvothermal method dissolving a metal and an organic ligandprecursor in a proper solvent and reacting the result at a hightemperature and a high pressure, a vapor diffusion method diffusing andpenetrating a different solvent capable of lowering solubility of aprecursor-dissolved solvent, a layer diffusion method forming a layerbetween two solutions containing different precursors to generatediffusion between the two layers, and the like.

The metal-organic framework (MOF) used in the present invention mayinclude a structural unit represented by the following Chemical Formula1.

[M_(x)(L)_(y)]  [Chemical Formula 1]

(In Chemical Formula 1,

-   -   M is one or more types of metals selected from the group        consisting of copper (Cu), zinc (Zn), iron (Fe), nickel (Ni),        chromium (Cr), scandium (Sc), cobalt (Co), titanium (Ti),        manganese (Mn), vanadium (V), aluminum (Al), magnesium (Mg),        gallium (Ga) and indium (In),    -   L is one or more types of organic metal ligands selected from        the group consisting of 1,4-benzenedicarboxylate (BDC),        1,3,5-benzenetricarboxlate (BTC),        1,1′-biphenyl-3,3′,5,5′-tetracarboxylate (BPTC) and        2-(N,N,N′,N′-tetrakis(4-carboxyphenyl)-biphenyl-4,4′-diamine        (TCBTDA), and    -   x is an integer of 2 to 6, and y is an integer of 2 to 12.)

In the present invention, the metal-organic framework is carbonized, andthe carbonized metal-organic framework (MOF) is used. A method ofcarbonizing the metal-organic framework is not particularly limited aslong as it is a method capable of including carbon in the metal-organicframework, and preferably, the metal-organic framework (MOF) may becarbonized under a temperature condition of carbonizing to 950° C. orhigher.

In the carbonized metal-organic framework (MOF) prepared as above,elements other than carbon in the MOF may be removed through thecarbonization process.

The carbonized metal-organic framework of the present invention preparedas above may have a specific surface area of 1000 m²/g to 4000 m²/g,preferably 1500 m²/g to 3000 m²/g, and most preferably 2,000 m²/g to2,500 m²/g. The specific surface area range being greater than 4000 m²/ghas a problem of causing more process time and costs than are necessaryto accomplish the specific surface area, and the range being less than1,000 m²/g has a problem in that sulfur may not be sufficiently loaded.

In addition, the metal-organic framework carbonized as above may have apore volume of 0.1 cc/g to 10 cc/g or greater, preferably 2.2 cc/g to3.0 cc/g, and most preferably 2.2 cc/g to 2.5 cc/g. The pore volumerange being less than 0.1 cc/g has a problem in that space to loadsulfur is not sufficient, and the range being greater than 10 cc/g has aproblem in that the specific surface area decreases. The pore volume maybe measured using common methods used in the art, and may be preferablymeasured using a barrett-joyner-halenda (BJH) method, a densityfunctional theory (DFT) method or the like.

Carbon-Sulfur Composite

The carbon-sulfur composite of the present invention includes a sulfurcompound introduced to at least a part of an outside surface and aninside of the carbonized metal-organic framework.

Various sulfur compounds used in a lithium-sulfur battery may be used asthe sulfur compound, and elemental sulfur (S₈), sulfur series compoundsor mixtures thereof are included. The sulfur series compound mayspecifically be selected from the group consisting of solid Li₂S_(n)(n≥≥1)-dissolved catholytes, organosulfur compounds and carbon-sulfurpolymers [(C₂S_(x))_(n), x=2.5 to 50, n≥≥2].

The carbon-sulfur composite may load sulfur in a high content due tovarious-sized pores and pores interconnected three-dimensionally andregularly ordered in the framework. Accordingly, when polysulfide havingsolubility is produced from an electrochemical reaction but is placedinside the carbon-sulfur composite, the three-dimensionally entangledstructure is maintained even with polysulfide elution, and a phenomenonof destroying a positive electrode structure may be suppressed. As aresult, a lithium-sulfur battery including the sulfur-carbon compositehas an advantage of exhibiting high capacity even with high loading. Theamount of sulfur loading of the carbon-sulfur composite according to thepresent invention may be from 1 mg/cm² to 20 mg/cm².

In the carbon-sulfur composite, a weight ratio of the carbonizedmetal-organic framework and the sulfur compound may be from 9:1 to 1:9,and preferably from 5:5 to 1:9. When the sulfur or sulfur compoundcontent is less than the above-mentioned range, the carbon-sulfurcomposite content increases, and as the carbon content increases, theamount of a binder added needs to be increased when preparing slurry.The increase in the amount of binder added ultimately increases sheetresistance of an electrode and performs a role of an insulatorpreventing electron migration, which may decline cell performance. Whenthe sulfur or sulfur compound content is greater than theabove-mentioned range, sulfur or sulfur compound that does not bind withthe composite aggregates themselves or re-eluted to the compositesurface making electron receiving difficult, and direct participation inthe electrode reaction may become difficult.

Method for Preparing Carbon-Sulfur Composite Including CarbonizedMetal-Organic Framework

The carbon-sulfur composite of the present invention is prepared through(a) preparing a carbonized metal-organic framework (MOF) by carbonizinga metal-organic framework (MOF) to 950° C. or higher; and (b) preparinga carbon-sulfur composite by mixing the metal-organic framework (MOF)carbonized in (a) with a sulfur compound.

First, the method for preparing a carbon-sulfur composite of the presentinvention includes (a) preparing a carbonized metal-organic framework(MOF) by carbonizing a metal-organic framework (MOF) to 950° C. orhigher.

In the step (a), the metal-organic framework (MOF) may be carbonized to950° C. or higher, preferably carbonized to 950° C. to 2,000° C., andmore preferably carbonized to 950° C. to 1,500° C.

A method of carbonizing the metal-organic framework is not particularlylimited as long as it is a method capable of including carbon in themetal-organic framework, and preferably, the metal-organic framework maybe carbonized under the atmosphere such as argon or nitrogen.

When carbonizing the metal-organic framework (MOF) to 950° C. or higheras in the step (a), carbon having a more developed pore structure isprepared, and using such carbon in a lithium sulfur battery hasadvantages of enhancing initial capacity and enhancing cycle retainingcapacity.

The carbonized metal-organic framework (MOF) of the present inventionprepared as above may have a specific surface area of 1000 m²/g to 4000m²/g, preferably 1500 m²/g to 3000 m²/g, and most preferably 2,000 m²/gto 2,500 m²/g. The specific surface area range being greater than 4000m²/g has a problem of causing more process time and costs than arenecessary to accomplish the specific surface area, and the range beingless than 1,000 m²/g has a problem in that sulfur may not besufficiently loaded.

In addition, the carbonized metal-organic framework (MOF) of the presentinvention prepared as above may have a pore volume of 0.1 cc/g to 10cc/g or greater, preferably 2.2 cc/g to 3.0 cc/g, and most preferably2.2 cc/g to 2.5 cc/g. The pore volume range being less than 0.1 cc/g hasa problem in that space to load sulfur is not sufficient, and the rangebeing greater than 10 cc/g has a problem in that the specific surfacearea decreases. The pore volume may be measured using common methodsused in the art, and may be preferably measured using abarrett-joyner-halenda (BJH) method, a density functional theory (DFT)method or the like.

Other properties of the metal-organic framework (MOF) used in the step(a) are the same as examined above.

After that, the carbon-sulfur composite of the present inventionincludes (b) preparing a carbon-sulfur composite by mixing themetal-organic framework (MOF) carbonized in (a) with a sulfur compound.

In the step (b), the method of mixing the sulfur compound is notparticularly limited in the present invention, and known methods may beused.

As one example of the method of mixing the sulfur compound, thecarbonized metal-organic framework and a sulfur compound powder may beuniformly mixed, the mixture is heated, and the melted sulfur compoundmay be impregnated into the carbonized metal-organic framework.

Herein, the sulfur compound may be mixed by flowing into the carbonizedmetal-organic framework close by through a capillary phenomenon.

The heating temperature may be from 115° C. to 180° C., and morespecifically from 150° C. to 160° C. According to one embodiment, thesulfur may also be uniformly coated around the carbonized metal-organicframework rather than voids between the carbonized metal-organicframeworks.

The heating time may be adjusted depending on the content of the sulfurcompound and the content of the carbonized metal-organic framework, andfor example, the heating time may be 10 seconds or longer or 30 secondsor longer, and 2 hours or shorter, 1 hour or shorter, 30 minutes orshorter or 10 minutes or shorter.

When the melting temperature is lower than 115° C., the sulfur compoundparticles are not melted, and the sulfur compound may not be properlyimpregnated into the carbonized metal-organic framework.

The impregnating of the sulfur compound may be carried out by dissolvinga sulfur compound in an organic solvent, and then growing the sulfurcompound through adding the carbonized metal-organic framework.

The organic solvent may be one selected from the group consisting ofethanol, toluene, benzene, N-methyl-2-pyrrolidone (NMP), dimethylsulfoxide (DMSO), acetone, chloroform, dimethylformamide, cyclohexane,tetrahydrofuran and methylene chloride, or a mixed solvent of two ormore thereof.

The impregnating of the sulfur compound may be carried out by mixing thecarbonized metal-organic framework and a sulfur compound powder andimpregnating using a ball mill method.

The mixing method may be carried out by introducing to a powder mixerfor a certain period of time. Herein, the mixing time may be 10 minutesor longer or 30 minutes or longer, and 10 hours or shorter, 5 hours orshorter or 2 hours or shorter.

When mixing the carbonized metal-organic framework and the sulfurcompound, a weight ratio of the carbonized metal-organic framework andthe sulfur compound may be from 9:1 to 1:9, and preferably from 5:5 to1:9. When the sulfur or sulfur compound content is less than theabove-mentioned range, the carbon-sulfur composite content increases,and as the carbon content increases, the amount of a binder added needsto be increased when preparing slurry. The increase in the amount ofbinder added ultimately increases sheet resistance of an electrode andperforms a role of an insulator preventing electron migration, which maydecline cell performance. When the sulfur or sulfur compound content isgreater than the above-mentioned range, sulfur or sulfur compound thatdoes not bind with the composite aggregates themselves or re-eluted tothe composite surface making electron receiving difficult, and directparticipation in the electrode reaction may become difficult.

Positive Electrode

The carbon-sulfur composite provided in the present invention is used asa positive electrode active material of a lithium secondary battery, andpreferably, may be used as a positive electrode active material of alithium-sulfur battery.

A lithium-sulfur battery includes sulfur as a positive electrode activematerial, and this has a problem of lithium polysulfide elution duringcharge and discharge. In the carbon-sulfur composite according to thepresent invention, sulfur may be uniformly distributed in the framework,and sulfur may be loaded in a high content due to pores with varioussizes and pores interconnected three-dimensionally and regularlyordered. Accordingly, a three-dimensionally entangled structure ismaintained even with polysulfide elution, and a phenomenon of destroyinga positive electrode structure may be suppressed. As a result, alithium-sulfur battery including the carbon-sulfur composite has anadvantage of obtaining high capacity even with high loading.

The positive electrode is prepared by coating a composition for forminga positive electrode active material layer on a positive electrodecurrent collector and drying the result. The composition for forming apositive electrode active material layer may be prepared by mixing thecarbon-sulfur composite described above, a conductor, a binder and asolvent.

Specifically, in order to additionally provide conductivity to theprepared carbon-sulfur composite, a conductor may be further added tothe positive electrode composition. The conductor performs a role forelectrons to smoothly migrate in the positive electrode, and is notparticularly limited as long as it has excellent conductivity and iscapable of providing a large surface area without inducing chemicalchanges to a battery, however, carbon-based materials are preferablyused.

As the carbon-based material, one type selected from the groupconsisting of graphite-based such as natural graphite, artificialgraphite, expanded graphite or graphene, active carbon-based, carbonblack-based such as channel black, furnace black, thermal black, contactblack, lamp black or acetylene black; carbon fiber-based, carbonnanostructures such as carbon nanotubes (CNT) or fullerene, andcombinations thereof may be used.

In addition to the carbon-based material, metallic fibers such as metalmesh; metallic powders such as copper (Cu), silver (Ag), nickel (Ni) andaluminum (Al); or organic conductive materials such as polyphenylenederivatives may also be used depending on the purpose. The conductivematerials may be used either alone or as a mixture.

In addition, in order to provide adhesion for a current collector to thepositive electrode active material, a binder may be further included inthe positive electrode composition. The binder needs to be favorablydissolved in a solvent, and needs to have proper impregnability of anelectrolyte liquid as well as favorably forming a conductive networkwith the positive electrode active material and the conductor.

The binder capable of being used in the present invention may be allbinders known in the art, and specifically, may be one type selectedfrom the group consisting of fluororesin-based binders includingpolyvinylidene fluoride (PVdF) or polytetrafluoroethylene (PTFE);rubber-based binders including styrene-butadiene rubber,acrylonitrile-butadiene rubber or styrene-isoprene rubber;cellulose-based binders including carboxymethylcellulose (CMC), starch,hydroxypropylcellulose Or regenerated cellulose; polyalcohol-basedbinders; polyolefin-based binders including polyethylene orpolypropylene; polyimide-based binders, polyester-based binders andsilane-based binders, or mixtures or copolymers of two or more typesthereof, but is not limited thereto.

The content of the binder resin may be from 0.5% by weight to 30% byweight based on the total weight of the positive electrode for alithium-sulfur battery, but is not limited thereto. When the binderresin content is less than 0.5% by weight, physical properties of thepositive electrode may decline eliminating the positive electrode activematerial and the conductor, and when the content is greater than 30% byweight, ratios of the active material and the conductor relativelydecrease in the positive electrode reducing battery capacity.

The solvent for preparing the positive electrode composition for alithium-sulfur battery in a slurry state needs to be readily dried, andmost preferably maintains the positive electrode active material and theconductor in a dispersed state without dissolution while favorablydissolving the binder. When the solvent dissolves the positive electrodeactive material, sulfur goes under in the slurry since sulfur has highspecific gravity (D=2.07) in the slurry, and sulfur is crowded on thecurrent collector when coating causing a problem in the conductivenetwork, and battery operation tends to have a problem.

As the solvent according to the present invention, water or organicsolvents may be used, and as the organic solvent, organic solventsincluding one or more types selected from the group consisting ofdimethylformamide, isopropyl alcohol, acetonitrile, methanol, ethanoland tetrahydrofuran may be used.

As for the mixing of the positive electrode composition, common methodsmay be used for the stirring using common mixers such as a paste mixer,a high shear mixer and a homo-mixer.

The positive electrode for a lithium-sulfur battery may be formed bycoating the positive electrode composition on a current collector, andvacuum drying the result. The slurry may be coated on the currentcollector to a proper thickness depending on the viscosity of the slurryand the thickness of the positive electrode to form, and preferably, thethickness may be properly selected in the range of 10 μm to 300 μm.

Herein, the method of coating the slurry is not limited, and forexample, methods of doctor blade coating, dip coating, gravure coating,slit die coating, spin coating, comma coating, bar coating, reverse rollcoating, screen coating, cap coating or the like may be carried out forthe preparation.

The positive electrode current collector is not particularly limited aslong as it may be prepared to generally have a thickness of 3 μm to 500μm, and has high conductivity without inducing chemical changes to abattery. For example, conductive metals such as stainless steel,aluminum, copper or titanium may be used, and preferably, an aluminumcurrent collector may be used. Such a positive electrode currentcollector may have various forms such as films, sheets, foil, nets,porous bodies, foams or non-woven fabrics.

Lithium-Secondary Battery

As one embodiment of the present invention, the lithium-secondarybattery may include the positive electrode described above; a negativeelectrode including lithium metal or an lithium alloy as a negativeelectrode active material; a separator provided between the positiveelectrode and the negative electrode; and an electrolyte impregnatedinto the negative electrode, the positive electrode and the separator,and including a lithium salt and an organic solvent.

The negative electrode may use a material capable of reversiblyintercalating or deintercalating lithium ions (Li⁺), a material capableof reversibly forming a lithium-containing compound by reacting withlithium ions, lithium metal or a lithium alloy as a negative electrodeactive material. Examples of the material capable of reversiblyintercalating or deintercalating lithium ions may include crystallinecarbon, amorphous carbon or a mixture thereof. Examples of the materialcapable of reversibly forming a lithium-containing compound by reactingwith lithium ions may include tin oxide, titanium nitrate or silicon.Examples of the lithium alloy may include alloys of lithium and metalsselected from the group consisting of Na, K, Rb, Cs, Fr, Be, Mg, Ca, Sr,Ba, Ra, Al and Sn.

In addition, while charging and discharging a lithium-sulfur battery,sulfur used as a positive electrode active material may be changed to aninactive material and attached on a lithium negative electrode surface.Inactive sulfur means sulfur that has gone through variouselectrochemical or chemical reactions and is not able to participate inan electrochemical reaction of a positive electrode any more, and theinactive sulfur formed on the lithium negative electrode surface has anadvantage of performing a role of a protective layer of the lithiumnegative electrode. Accordingly, lithium metal and inactive sulfurformed on this lithium metal, for example, lithium sulfide, may be usedas the negative electrode.

The negative electrode of the present invention may additionally furtherinclude, in addition to the negative electrode active material, apretreatment layer formed with a lithium ion conductive material, and alithium metal protective layer formed on the pretreatment layer.

The separator provided between the positive electrode and the negativeelectrode separates or insulates the positive electrode and the negativeelectrode from each other, and enables lithium ion transfer between thepositive electrode and the negative electrode, and may be formed withporous non-conductive or insulating materials. As an insulator havinghigh ion permeability and mechanical strength, such a separator may bean independent member such as a thin film or a film, or a coating layeradded to the positive electrode and/or the negative electrode. Inaddition, when using a solid electrolyte such as a polymer as theelectrolyte, the solid electrolyte may also be used as the separator.

The separator preferably has a pore diameter of generally 0.01 μm to 10μm and a thickness of generally 5 μm to 300 μm, and as such a separator,a glass electrolyte, a polymer electrolyte, a ceramic electrolyte or thelike may be used. For example, olefin-based polymers having chemicalresistance and hydrophobicity such as polypropylene, glass fiber, orsheets, non-woven fabrics, kraft papers and the like made ofpolyethylene and the like are used. Typical examples commerciallyavailable may include Celgard series (CelgardR 2400, 2300, product ofHoechest Celanese Corp.), polypropylene separator (product of UbeIndustries Ltd. or product of Pall RAI), polyethylene series (Tonen orEntek) and the like.

The electrolyte separator in a solid state may include a non-aqueousorganic solvent in approximately less than 20% by weight, and in thiscase, a proper gelling agent may be further included in order to reducefluidity of the organic solvent. Typical examples of such a gellingagent may include polyethylene oxide, polyvinylidene fluoride,polyacrylonitrile and the like.

The electrolyte impregnated into the negative electrode, the positiveelectrode and the separator is, as a lithium salt-containing non-aqueouselectrolyte, formed with a lithium salt and an electrolyte liquid, andas the electrolyte liquid, non-aqueous organic solvents, organic solidelectrolytes, inorganic solid electrolytes and the like are used.

The lithium salt of the present invention may include, as a materialfavorably dissolved in a non-aqueous organic solvent, may include one ormore selected from the group consisting of LiSCN, LiCl, LiBr, LiI,LiPF₆, LiBF₄, LiSbF₆, LiAsF₆, LiB₁₀Cl₁₀, LiCH₃SO₃, LiCF₃SO₃, LiCF₃CO₂,LiClO₄, LiAlCl₄, Li(Ph)₄, LiC(CF₃SO₂)₃, LiN(FSO₂)₂, LiN(CF₃SO₂)₂,LiN(C₂F₅SO₂)₂, LiN(SFO₂)₂, LiN(CF₃CF₂SO₂)₂, chloroborane lithium, loweraliphatic carboxylic acid lithium, lithium tetraphenylborate, lithiumimide and combinations thereof.

The concentration of the lithium salt may be from 0.2 M to 2 M,specifically from 0.6 M to 2 M and more specifically from 0.7 M to 1.7 Mdepending on various factors such as an accurate composition of theelectrolyte solvent mixture, solubility of the salt, conductivity of thedissolved salt, charge and discharge conditions of a battery, a workingtemperature, and other factors known in the lithium battery field. Whenused in less than 0.2 M, conductivity of the electrolyte may decreasecausing decline in the electrolyte performance, and when used in greaterthan 2 M, viscosity of the electrolyte increases leading to a decreasein the lithium ion (Li⁺) mobility.

The non-aqueous organic solvent needs to favorably dissolve the lithiumsalt, and examples of the non-aqueous organic solvent of the presentinvention may include aprotic organic solvents such asN-methyl-2-pyrrolidinone, propylene carbonate, ethylene carbonate,butylene carbonate, dimethyl carbonate, diethyl carbonate, ethylmethylcarbonate, gamma-butyrolactone, 1,2-dimethoxyethane, 1,2-diethoxyethane,tetrahydroxy franc, 2-methyl tetrahydrofuran, dimethyl sulfoxide,1,3-dioxolane, 4-methyl-1,3-dioxene, diethyl ether, formamide,dimethylformamide, dioxolane, acetonitrile, nitromethane, methylformate, methyl acetate, phosphoric acid triester, trimethoxymethane,dioxolane derivatives, sulfolane, methylsulfolane,1,3-dimethyl-2-imidazolidinone, propylene carbonate derivatives,tetrahydrofuran derivatives, ether, methyl propionate or ethylpropionate may be used, and the organic solvent may be used either aloneor as a mixture of two or more organic solvents.

As the organic solid electrolyte, for example, polyethylene derivatives,polyethylene oxide derivatives, polypropylene oxide derivatives,phosphoric acid ester polymers, polyalginate lysine, polyester sulfide,polyvinyl alcohol, polyvinylidene fluoride, polymers including an ionicdissociation group, and the like may be used.

As the inorganic solid electrolyte, for example, nitrides, halides,sulfates and the like of Li such as Li₃N, LiI, Li₅NI₂, Li₃N—LiI—LiOH,LiSiO₄, LiSiO₄—LiI—LiOH, Li₂SiS₃, Li₄SiO₄, Li₄SiO₄—LiI—LiOH orLi₃PO₄—Li₂S—SiS₂ may be used.

With the purpose of improving charge and discharge properties and flameretardancy, for example, pyridine, triethylphosphite, triethanolamine,cyclic ether, ethylenediamine, n-glyme, hexaphosphoric acid triamide,nitrobenzene derivatives, sulfur, quinoneimine dyes, N-substitutedoxazolidinone, N,N-substituted imidazolidine, ethylene glycol dialkylether, ammonium salts, pyrrole, 2-methoxyethanol, aluminum trichlorideor the like may also be added to the electrolyte of the presentinvention. In some cases, halogen-containing solvents such as carbontetrachloride and trifluoroethylene may be further included in order toprovide nonflammability, carbon dioxide gas may be further included inorder to enhance high temperature storage properties, andfluoro-ethylene carbonate (FEC), propene sultone (PRS), fluoro-propylenecarbonate (FPC) and the like may be further included.

The electrolyte may be used as a liquid-state electrolyte or as anelectrolyte separator form in a solid state. When using as aliquid-state electrolyte, a separator formed with porous glass,plastics, ceramics or polymers is further included as a physicalseparator having a function of physically separating electrodes.

DETAILED DESCRIPTION OF THE INVENTION

Hereinafter, preferred examples are provided in order to illuminate thepresent invention, however, the following examples are for illustrativepurposes only, and it is obvious to those skilled in the art thatvarious changes and modifications may be made within the category andtechnological ideas of the present invention, and such changes andmodifications also fall within the scope of the attached claims.

EXAMPLE

Preparation of Sulfur-Carbon Composite

Example 1

0.8 g of Zn(NO₃)₂·6H₂O and 0.149 g of 1,4-benzenedicarboxylic acid(H₂BDC) (molar ratio=3:1) were introduced to a 50 mL container with 30mL of DMF. The reaction solution was heated for 1 day in a 120° C. oven.A crystalline product was washed twice with DMF and MC. The crystallineproduct was washed several times with anhydrous DMF and anhydrous MC.The product was dried overnight in a 150° C. vacuum oven to prepare ametal-organic framework (MOF-5) (0.28 g, yield=91%).

The obtained metal-organic framework was placed in an oven and thencarbonized for 6 hours at 1,000° C. By using the obtained carbonizedmetal-organic framework, sulfur and the carbonized metal-organicframework were mixed to have a weight ratio of 7:3, and the result washeat treated for 30 minutes at 155° C. to prepare a sulfur-carboncomposite.

Comparative Example 1

A sulfur-carbon composite was prepared in the same manner as in Example1 except that the sulfur-carbon composite was prepared using activatedcarbon instead of the carbonized metal-organic framework.

Comparative Example 2

A sulfur-carbon composite was prepared in the same manner as in Example1 except that a Ti₃C₂T_(x) @Meso-C/S composite prepared using a methodof “Adv. Funct. Mater. 2016, 26, 8746-8756” was used instead of thecarbonized metal-organic framework.

Comparative Example 3

A sulfur-carbon composite was prepared in the same manner as in Example1 except that the metal-organic framework was placed in an oven and thencarbonized at 900° C.

Experimental Example 1: Evaluation on Properties of CarbonizedMetal-Organic Framework

(Analysis on Surface Photographing)

For the sulfur-carbon composite (MOF-5 (1000)) prepared in Example 1 andthe sulfur-carbon composite (MOF-5 (900)) prepared in ComparativeExample 3, SEM images were photographed (HITACHI S-4800), and theresults are shown in a of FIG. 4 (Example 1) and b of FIG. 4(Comparative Example 3).

(Analysis on N₂ Adsorption/Desorption Isotherm)

To each of the carbonized metal-organic framework (MOF-5 (1000))prepared in Example 1 and the carbonized metal-organic framework (MOF-5(900)) prepared in Comparative Example 3, vacuum was applied for 2 hoursat room temperature, and an N₂ adsorption/desorption isotherm wasmeasured (AUTOSORB-iQ-MP instrument, manufactured by QuantachromeInstruments), and the results are shown in FIG. 1 . An N₂adsorption/desorption isotherm for the activated carbon prepared inComparative Example 1 is shown in FIG. 3 .

Through FIG. 1 , it was seen that the carbonized metal-organic framework(MOF-5 (1000)) prepared in Example 1 had a relatively larger specificsurface area compared to the carbonized metal-organic framework (MOF-5(900)) prepared in Comparative Example 3. In addition, through FIG. 3 ,it was seen that they both had a relatively smaller specific surfacearea compared to the activated carbon prepared in Comparative Example 1.

(Analysis on Quenched Solid Density Functional Theory)

For the carbonized metal-organic framework (MOF-5 (1000)) prepared inExample 1 and the carbonized metal-organic framework (MOF-5 (900))prepared in Comparative Example 3, pore size distribution is shown inFIG. 2 using a quenched solid density functional theory (QSDFT) method(slit/cylindrical/sphere pores) (AUTOSORB-iQ-MP instrument, manufacturedby Quantachrome Instruments).

Through FIG. 2 , it was seen that the carbonized metal-organic framework(MOF-5 (1000)) prepared in Example 1 contained more meso-sized porescompared to the carbonized metal-organic framework (MOF-5 (900))prepared in Comparative Example 3.

Through the results, a carbonization temperature-dependent BET wasobtained, and the results are shown in Table 1.

TABLE 1 Specific Pore Carbonization Surface Area Volume Temperature[m²/g] [cc/g] Example 1 MOF-5 (1000° C.) 2178 2.36 Comparative MOF-5(900° C.) 1947 1.844 Example 3 Comparative Activated 3890 2.17 Example 1Carbon

Experimental Example 2: Evaluation on Battery Performance

Using the prepared sulfur-carbon composite, slurry was prepared with thesulfur-carbon composite:conductor:binder in a weight ratio of 90:5:5,and the slurry was coated on aluminum foil current collector having athickness of 20 μm to prepare an electrode. Herein, carbon black wasused as the conductor, styrene butadiene rubber andcarboxymethylcellulose were used as the binder, and the loading amountwas 3 mAh/cm².

(Evaluation on Battery Performance)

For the lithium-sulfur battery manufactured using each of thesulfur-carbon composite (MOF-5 (1000)) prepared in Example 1 and thesulfur-carbon composites (MOF-5 (900)) prepared in Comparative Examples1 to 3, changes in the charge and discharge properties were tested usinga charge and discharge measurement device. Using the obtained battery,initial discharge/charge was progressed with 0.1 C/0.1 C for 2.5 cycles,then 3 cycles was performed with 0.2 C/0.2 C, and thereafter, 10 cycleswith 0.5 C/0.3 C and 3 cycles with 0.2 C/0.2 C were repeated. Theresults were measured and are shown in FIG. 5 to FIG. 8 .

FIG. 5 is a graph showing initial charge and discharge properties of thelithium-sulfur batteries manufactured in Example 1 and ComparativeExample 3, FIG. 6 is a graph showing initial charge and dischargeproperties of the lithium-sulfur battery manufactured in ComparativeExample 1, and FIG. 7 is a graph showing initial charge and dischargeproperties of the lithium-sulfur battery manufactured in ComparativeExample 2.

When referring to FIG. 5 , the lithium-sulfur battery manufactured usingthe sulfur-carbon composite of Example 1 prepared carbon with a moredeveloped pore structure as the carbonization temperature of themetal-organic framework (MOF) increased to 1000° C., and used the carbonin a lithium sulfur battery, and it was seen that Example 1 had enhancedinitial capacity and enhanced cycle retaining capacity compared toComparative Example 3 having a less developed pore structure.

On the other hand, when referring to FIG. 6 , it was seen that thelithium-sulfur battery manufactured using the sulfur-carbon composite ofComparative Example 1 did not exhibit initial discharge capacity while adischarge overvoltage was highly applied. This indicates that, as wellas a BET and a pore volume that carbon has, the pore distribution hassignificant effects on cell performance. In other words, this is due tothe fact that, in the activated carbon, micropores have dominantdistribution.

In addition, when referring FIG. 7 , it was seen that the sulfur-carboncomposite of Comparative Example 2 was prepared in a similar manner asin Example 1, but had initial capacity of approximately 1000 mAh/g,which is lower than Example 1.

FIG. 8 is a graph showing charge and discharge efficiency of thelithium-sulfur batteries manufactured in Example 1 and ComparativeExample 3. When referring to FIG. 8 , it was seen that thelithium-sulfur battery manufactured using the sulfur-carbon composite ofExample 1 had higher discharge retaining capacity when progressing thecycle.

1. A carbon-sulfur composite comprising: a carbonized metal-organic framework; and a sulfur compound introduced to at least a part of an outside surface and an inside of the carbonized metal-organic framework, wherein the carbonized metal-organic framework has a specific surface area of 1000 m²/g to 1500 m²/g, and the carbonized metal-organic framework has a pore volume of 0.1 cc/g to 10 cc/g.
 2. The carbon-sulfur composite of claim 1, wherein the carbonized metal-organic framework has a specific surface area of 1000 m²/g.
 3. The carbon-sulfur composite of claim 1, wherein the carbonized metal-organic framework has a specific surface area of 1500 m²/g.
 4. The carbon-sulfur composite of claim 1, wherein the carbonized metal-organic framework has a pore volume of 2.2 cc/g to 3.0 cc/g.
 5. The carbon-sulfur composite of claim 1, wherein the metal-organic framework (MOF) includes a structural unit represented by the following Chemical Formula 1: [M_(x)(L)_(y)]  [Chemical Formula 1] in Chemical Formula 1, M is one or more types of metals selected from the group consisting of copper (Cu), zinc (Zn), iron (Fe), nickel (Ni), chromium (Cr), scandium (Sc), cobalt (Co), titanium (Ti), manganese (Mn), vanadium (V), aluminum (Al), magnesium (Mg), gallium (Ga) and indium (In); L is one or more types of organic metal ligands selected from the group consisting of 1,4-benzenedicarboxylate (BDC), 1,3,5-benzenetricarboxlate (BTC), 1,1′-biphenyl-3,3′,5,5′-tetracarboxylate (BPTC) and 2-(N,N,N′,N′-tetrakis(4-carboxyphenyl)-biphenyl-4,4′-diamine (TCBTDA); and x is an integer of 2 to 6, and y is an integer of 2 to
 12. 6. The carbon-sulfur composite of claim 1, comprising the carbonized metal-organic framework (MOF) and the sulfur compound in a weight ratio of 9:1 to 1:9.
 7. A method for preparing a carbon-sulfur composite according to claim 1, comprising: (a) preparing a carbonized metal-organic framework (MOF) by carbonizing a metal-organic framework (MOF) to 950° C. or higher; and (b) preparing a carbon-sulfur composite by mixing the metal-organic framework (MOF) carbonized in (a) with a sulfur compound.
 8. The method for preparing a carbon-sulfur composite of claim 7, wherein, in (a), the metal-organic framework (MOF) is carbonized to 950° C. to 2,000° C.
 9. The method for preparing a carbon-sulfur composite of claim 7, wherein, in (a), the metal-organic framework (MOF) is carbonized to 950° C. to 1,500° C.
 10. The method for preparing a carbon-sulfur composite of claim 7, wherein, in (a), the carbonized metal-organic framework has a specific surface area of 1000 m²/g to 1500 m²/g, and a pore volume of 0.1 cc/g to 10 cc/g.
 11. The method for preparing a carbon-sulfur composite of claim 7, wherein the metal-organic framework (MOF) includes a structural unit represented by the following Chemical Formula 1: [M_(x)(L)_(y)]  [Chemical Formula 1] in Chemical Formula 1, M is one or more types of metals selected from the group consisting of copper (Cu), zinc (Zn), iron (Fe), nickel (Ni), chromium (Cr), scandium (Sc), cobalt (Co), titanium (Ti), manganese (Mn), vanadium (V), aluminum (Al), magnesium (Mg), gallium (Ga) and indium (In); L is one or more types of organic metal ligands selected from the group consisting of 1,4-benzenedicarboxylate (BDC), 1,3,5-benzenetricarboxlate (BTC), 1,1′-biphenyl-3,3′,5,5′-tetracarboxylate (BPTC) and 2-(N,N,N′,N′-tetrakis(4-carboxyphenyl)-biphenyl-4,4′-diamine (TCBTDA); and x is an integer of 2 to 6, and y is an integer of 2 to
 12. 12. The method for preparing a carbon-sulfur composite of claim 7, wherein, in (b), the carbonized metal-organic framework (MOF) and the sulfur compound are mixed in a weight ratio of 9:1 to 1:9.
 13. A positive electrode comprising the carbon-sulfur composite of claim
 1. 14. The positive electrode of claim 13, which is for a lithium-sulfur battery.
 15. A lithium secondary battery comprising: the positive electrode of claim 13; a negative electrode; and an electrolyte. 